CN1321217C - Method for producing aluminum alloy composite material for heat exchanger and aluminum alloy composite material - Google Patents
Method for producing aluminum alloy composite material for heat exchanger and aluminum alloy composite material Download PDFInfo
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- CN1321217C CN1321217C CNB038050331A CN03805033A CN1321217C CN 1321217 C CN1321217 C CN 1321217C CN B038050331 A CNB038050331 A CN B038050331A CN 03805033 A CN03805033 A CN 03805033A CN 1321217 C CN1321217 C CN 1321217C
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/016—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of aluminium or aluminium alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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Abstract
A method for producing an aluminum alloy composite material for a heat exchanger, which contains the steps of: homogenizing an aluminum alloy core alloy by keeping at 530 DEG C or more for 15 hours or more; fitting an Al-Si-series filler alloy on one side or on both sides of the core alloy; hot rolling; cold rolling; intermediate annealing, to completely recrystallize the core alloy; and giving a strain of 1 to 10%, wherein the aluminum alloy core alloy contains 0.01 to 1.0% by mass of Si, 0.1 to 2.0% by mass of Fe, 0.1 to 2.0% by mass of Cu, 0.5 to 2.0% by mass of Mn, and less than 0.2% by mass (including 0% by mass) of Ti, with the balance being Al and inevitable impurities; and an aluminum alloy composite material produced by the method.
Description
Technical field
The present invention relates to a kind of manufacture method that is used for the Al alloy composite of heat exchanger, and, the present invention relates to the Al alloy composite of this method manufacturing.
Background technology
Usually, the core of heat exchanger such as vaporizer and condenser, is made as shown in Figure 1, and its step comprises: press forming one matrix material (brazing sheet) forms fold, and this matrix material is made up of the aluminium alloy core alloy that the two sides is covered with filler alloys; Pile up two plates that the refrigerant pass forming element 1 of fold is arranged, vertically to form refrigerant pass 2; These plates of soldering then.In the figure, the fin of a fold of reference number 3 expressions; Reference number 4 expression soldering points (flat part), vertical direction mobile refrigerant pass of reference number 5 expressions.Because for satisfying the needs of lightweight material, the plate thickness of described material is reducing in recent years, so need improve physical strength, erosion resistance and the braze ability of the aluminium element of the heat exchanger that is used to form refrigerant pass 2.
The heat of soldering makes filler alloys be diffused into as brazing sheet and forms in the aluminium alloy core alloy of aluminum alloy materials of above-mentioned refrigerant pass that wherein filler alloys penetrates in the core alloy.Because the filler alloys quantity that the diffusion of filler alloys causes supplying to the soldering part reduces, defective brazing may take place, such as the anti-pressure ability decline of soldering part soldering discontinuous (because defective that the filler alloys of supply causes inadequately) and heat exchanger.In addition, in filler alloys was diffused into the zone of core alloy, core alloy inherent intensity and erosion resistance had reduced greatly, and after the soldering heating, the reduction that the performance of heat exchanger is also suitable.
In order to prevent such diffusion of filler alloys, a method is arranged, give the prestrain of the rolling stock 1-5% of an aluminium manganese-base alloy, added an amount of copper and iron in this rolling stock, heat makes the suitable recrystallize of this alloy in brazing process.Yet, in this case, such problem is arranged, make the plasticity of this generation alloy reduce owing to applying the mechanical hardening that strain causes, and in forming process, crack.Therefore, such countermeasure can not be satisfactory.
Summary of the invention
The present invention proposes a kind of manufacture method that is used for the Al alloy composite of heat exchanger, may further comprise the steps: by keeping core alloy 530 ℃ or higher 15 hours or longlyer come this aluminium alloy core alloy of homogenizing; A side or both sides aluminium coating silicon series filler alloys at this core alloy; The coating alloy that hot rolling generated; The coating alloy of cold rolling this hot rolling; The coating alloy of this cold rolling mistake is carried out the process annealing processing, so that the abundant recrystallize of this core alloy; Apply the strain of 1-10% to the alloy of this generation, wherein the mass percent of aluminium alloy core alloy (being reduced to % hereinafter) comprises the silicon of 0.01-1.0%, the iron of 0.1-2.0%, the copper of 0.1-2.0%, the manganese of 0.5-2.0%, the titanium that is less than 0.2% (comprising 0%), remaining sum are aluminium and unavoidable impurities.
In addition, the present invention proposes a kind of Al alloy composite that is used for heat exchanger of manufacturing by the way.
Other and more the features and advantages of the present invention will more fully show by following description in conjunction with the accompanying drawings.
Description of drawings
Fig. 1 is a part skeleton view of explaining a kind of car heat exchanger (scatterer).
Embodiment
According to the present invention, provide following mode:
(1) a kind of manufacture method that is used for the Al alloy composite of heat exchanger comprises step: by with core alloy 530 ℃ or higher maintenance 15 hours or longlyer come homogenizing aluminium alloy core alloy; A side or both sides aluminium coating silicon series alloy at core alloy; The coating alloy that hot rolling generated; The coating alloy of cold rolling this hot rolling; The coating alloy of this cold rolling mistake is carried out the process annealing processing so that the abundant recrystallize of core alloy; Apply the strain of 1-10% for the alloy that generates, wherein the mass percent of aluminium alloy core alloy (being reduced to % hereinafter) comprises the silicon of 0.01-1.0%, the iron of 0.1-2.0%, the copper of 0.1-2.0%, the manganese of 0.5-2.0%, the titanium that is less than 0.2% (comprising 0%), remaining sum are aluminium and unavoidable impurities.
(2) as the described method of clauses and subclauses (1), wherein homogenization step comprises that the maintenance core alloy is at 530 ℃ or higher 2 hours and longer, be cooling subsequently, core alloy kept 1 hour or longer at 500-560 ℃ during cooling, rather than 530 ℃ or higher maintenance 15 hours or longer.
(3) as clauses and subclauses (1) or (2) described method, wherein process annealing comprises that the coating alloy with cold rolling mistake kept 1 hour or more at 320-450 ℃.
(4) as clauses and subclauses (1) or (2) described method, wherein process annealing comprises: with 30 ℃/minute or faster rate of heating heat the coating alloy of cold rolling mistake; Under 300-550 ℃, described coating alloy is kept 1-180 second; Then with 30 ℃/minute or the generation of speed of cooling cooling faster alloy.
(5), after applying the strained step of 1-10%, also comprised the step of thermal treatment (annealing at last) as any described method in clauses and subclauses (1) or (4).
(6) as the described method of clauses and subclauses (5), wherein after the strain that applies 1-10%, described thermal treatment is included in 200-380 ℃ and kept 1 hour or longer.
(7) as the described method of clauses and subclauses (5), wherein after the strain that applies 1-10%, described thermal treatment comprises that step has: with 30 ℃/minute or rate of heating heating faster; Keep 1-180 second down at 250-420 ℃; Then with 30 ℃/minute or speed of cooling cooling faster.
(8) with producing the Al alloy composite that is used for heat exchanger as clauses and subclauses (1)-(7) described method.
Further describe the present invention hereinafter.
The inventor has done a lot of research and has penetrated the material of core alloy or analogue to research and develop a kind of filler alloys that can stop with good plasticity, and has obtained following achievement.By a kind of core alloy that adds the aluminium manganese-base alloy of amount of copper and iron of homogenization, after covering this filler alloys on this core alloy, apply prestrain for rolling material, use predetermined thermal treatment in case of necessity, stop filler alloys to penetrate core alloy like this.The inventor finds that above-mentioned processing can improve plasticity when keeping erosion resistance and intensity, finished the present invention.
The alloying element of forming used core alloy among the present invention is at first described.
Silicone content accounts for the 0.01-1.0% of mass percent (hereinafter referred is %), because when increase filler alloys quantity formed fillet, silicon can stop the filler alloys diffusion, and has the function of the strength of materials after the raising soldering.Be lower than under the content situation of above-mentioned nil-norm, the effect of silicon can't embody, and exceeds at silicone content under the situation of above-mentioned top limit, may cause a kind of fusion phenomenon that is called as burning (burning) under brazing temperature.Preferred silicone content is in the scope of 0.1-0.6%.
Iron and copper are effective to improving intensity and strengthening the recrystallize ability.By finish recrystallize before filler alloys penetrates, filler alloys penetrated in the core alloy when these elements had suppressed the soldering heating.
Iron level is limited in the scope of 0.1-2.0%, because the effect that is lower than iron under the situation of above-mentioned nil-norm when its content is not enough to embody, erosion resistance reduces under the situation of above-mentioned top limit and be higher than when its content.The preferred content scope of iron is 0.1-1.1%, more preferably 0.2-0.8%.
Copper content is limited in the scope of 0.1-2.0%, because the effect that is lower than iron under the situation of above-mentioned nil-norm when its content is not enough to embody, base mateiral (matrix (matrix)) can fusing under the situation of above-mentioned top limit and be higher than when its content.The preferred content scope of iron is 0.1-1.1%, more preferably 0.2-0.8%.
The effect that copper has the enhancing filler alloys to penetrate, this effect suppresses by adding iron simultaneously with copper.
Manganese improves intensity by form sosoloid with aluminum matrix in the soldering step.Manganese content is limited in the scope of 0.5-2.0%, because be not enough to embody the effect that increases manganese when its content is lower than 0.5%, its content is higher than the 2.0% rolling rational faculty and plasticity can reduce and work as.The special preferred content scope of manganese is 0.9-1.6%.
Titanium is used to improve erosion resistance.Its content was limited in being less than 0.2% (comprising 0%) because when its content be 0.2% or more for a long time, the recrystallize ability of the core alloy in the soldering step (aluminium alloy) is suppressed.
Among the present invention, the residue content except above-mentioned alloying element in the core alloy is aluminium and unavoidable impurities.Only otherwise influence effect of the present invention, the kind and the content of unavoidable impurities have no particular limits.
Secondly, will the reason of homogeneous treatment condition among restriction the present invention be described.
During the filler alloys fusing, the filler alloys that takes place during the soldering heating will advance along the crystal crystal boundary or the pseudocone crystal boundary of core alloy to the diffusion of core alloy.When brazing sheet is dead annealed material, core alloy can not heated recrystallize by soldering.Thereby filler alloys is along the crystal boundary diffusion of core alloy.Thereby because the crystal grain of core alloy is meticulousr, filler alloys is with easier diffusion, and the diffusion of filler alloys is easier to be predicted.
On the other hand, when core alloy during by shaping brazing sheet generation strain, because the existence of recrystal grain crystal boundary and pseudocone crystal boundary, core alloy will be heated and the part recrystallize in the soldering step.Because the sedimentary distribution in the core alloy can influence the recrystallize behavior in this stage, sedimentary different distributions will be brought the different states of filler alloys diffusion, and this can cause the variation of soldering heating back as the characteristic of intensity and erosion resistance.Thereby in order to reduce the change of state of filler alloys diffusion, fully the distribution of homogenizing core alloy and settling thing is effective.
Preferably, as the homogenization condition, core alloy makes and stablizes the structure of core alloy by being formed on the sedimentary sosoloid that forms in the casting process of cooling by 530 ℃ or higher maintenance 15 hours or longlyer come homogenization.Yet the upper limit of homogenization temperature should be controlled in the scope that can not melt core alloy.As for the lower limit of homogenization time, when the homogenization time was shorter than the above-mentioned time, sedimentary sosoloid can not fully be shaped, and this can cause occurring the diffusion of filler alloys in the soldering step.As long as the feasible fusing that can not cause core alloy of homogenization time Be Controlled, just there is no particular limitation for the upper limit of homogenization time, and the preferred time is the acceptable scope an economy.The hold-time that above-mentioned homogenization is handled is from counting when the temperature that heats the aluminium alloy core alloy surpasses 530 ℃, to hanging down to 530 ℃ or lower when the temperature of cooling aluminium alloy core alloy.
In addition, for obtaining the material of the less diffusion of a kind of filler alloys, following homogenization treatment condition are effective.Core alloy is 530 ℃ or higher maintenance 2 hours or more, be preferably 15 hours or more, preferred this core alloy in 570-620 ℃ temperature range, kept 2 hours or more after enter cooling step, wherein this core alloy kept 1 hour or more in 500-560 ℃ temperature range.Throw out in the core alloy is enhanced to form a kind of sosoloid under 530 ℃ or higher temperature, preferably at 570-620 ℃, and is strengthened by remain on 500-560 ℃ of precipitating action in cooling step.Like this, the structure of core alloy is more stable, and suppresses filler alloys and add in soldering and pine for diffusion.
Because matrix material of the present invention has good plasticity as the material require that is used for heat exchanger before soldering, so core alloy should perfect recrystallization in the process annealing step.Thereby, the condition optimization of process annealing be to keep 1 hour or more down at 320-450 ℃.Annealing temperature is too low or annealing time is too short in the process annealing step, and core alloy may be incomplete recrystallized.The annealing temperature that surpasses 450 ℃ is unfavorable economically, and may make and grow up to crystal boundaries slightly the particle of (greatly) has reduced plasticity.
For further improving plasticity, preferred process annealing condition be core alloy with 30 ℃/minute or faster rate of heating be heated, keep 1-180 second under the temperature in 300-550 ℃ of scope, then with 30 ℃/minute or faster speed of cooling be cooled.This process makes to be shaped and is guaranteed the more homogeneous and the careful because size on the recrystal grain border of the aluminum alloy materials of core alloy becomes.Heating rate or rate of cooling are too slow, or keep temperature too high, perhaps the hold-time oversize be worthless because the crystallographic grain of aluminum alloy materials becomes too thick.Keep too low or hold-time of temperature too weak point also be worthless because the recrystallize in the annealing process becomes insufficient.
When a brazing sheet of being made up of the perfect recrystallization core alloy is used to be shaped, bearing the instability diffusion that causes filler alloys on the particular job strained section.The dependent variable that has confirmed to cause above-mentioned filler alloys diffusion 0-less than 1% scope in, this core alloy is made up of the aluminium manganese-base alloy.On the other hand, soldering heating bear 1% or more strained core alloy can not cause the diffusion of filler alloys in brazing process because before filler alloys is melted, the recrystallize of core alloy is finished at a low-temperature region.Thereby, in aftermentioned shaping and soldering heat-processed, can obtain a kind of diffusion matrix material seldom by applying one 1% or higher work prestrain to brazing sheet in advance, this work prestrain is bigger than the dependent variable that causes the filler alloys diffusion in the brazing sheet.When applying strain less than 1% the time, be diffused on the part of low work strain and take place.On the other hand, the strain that applies above 10% is worthless, because the plasticity of material has reduced.
In addition, in heat exchanger, some are a long felt need for good plasticity, the plate material of using such as vaporizer.In order to adapt to such use, if necessary, after applying above-mentioned strain, can use a kind of thermal treatment (annealing at last).Especially when applying strain at 1-3%, apply after the strain thermal treatment not necessarily.Yet, apply after the strain as do not heat-treat, be preferably in the process annealing step with 30 ℃/minute or faster rate of heating be heated, keep 1-180 after second at 300-550 ℃, with 30 ℃/minute or faster speed of cooling be cooled.On the other hand, when applying strain, particularly preferredly after applying strain, heat-treat at 3-10%.
About applying specific heat-treat condition after the strain, brazing sheet kept 1 hour down or more heat treatment mode at 200-380 ℃, perhaps brazing sheet with 30 ℃/minute or faster rate of heating be heated, keep 1-180 after second at 250-420 ℃, with 30 ℃/minute or faster speed of cooling be cooled, such or similarly heat treatment mode be better to improving forming property.The heat-treat condition that exceeds the foregoing description scope may not be very remarkable to the raising of plasticity.
Variously be used for filler metal of the present invention and not only be confined to use aluminium silicon series filler alloys especially.Various known filler alloys, such as, alloy JIS4045 also can use.The covering method of filler alloys and core alloy without limits is such as overlay environment and coating ratio.In the scope of not damaging effect of the present invention, can suitably use ordinary method.
As long as obtained preset thickness in each manufacturing step, hot rolling and cold rolling (such as draft) and can suitably use ordinary method also without limits among the present invention.
The Al alloy composite of method manufacturing of the present invention can be used for tube plate and case (headerplates and tanks), can be used for the refrigerant pass pipe as vaporizer and this class heat exchanger of scatterer in addition.And matrix material of the present invention also can be used for heating tube or prolong or similar thing, and can be used for any member, if its plate thickness preferably is taken at 0.6mm or still less, promptly is applicable to matrix material of the present invention.
The Al alloy composite that is used for heat exchanger of the present invention can be used as the braze material that soldering connects product, penetrates core alloy etc. to stop filler alloys, and has good plasticity.Further, this manufacture method of the present invention is to make the preferred method of the Al alloy composite that is used for heat exchanger.
The produced Al alloy composite of manufacture method of the present invention has good erosion resistance and high intensity, and the diffusion of filler alloys is all very little on any shaping degree.This material also is suitable for being shaped, and applies the plasticity reduction that strain causes because the control heat-treat condition can stop.
Thereby when using as heat exchanger material, the present invention can produce significant industrial effect, such as guaranteeing secular reliability.
Example
The present invention quotes example hereinafter and Comparative Examples describes in detail, but the present invention is in no way limited to these examples.
Each personal mold of the JIS4045 alloy of the aluminium alloy of core alloy and filler alloys is cast, and wherein this aluminium alloy comprises 0.25% silicon, 0.5% iron, and 0.15% copper, 1.1% manganese and all the other are aluminium.Core alloy homogenization under the temperature of table 1 row and hold-time condition, and finishing touch is processed into the thickness of 40mm.About filler alloys, its blank is processed by finishing processing and hot rolling, and covers the two sides of core alloy, and the coating ratio of each face is 10%.Generate coating alloy and be heated to 500 ℃, hot rolling is thick to 3.5mm, and is cold rolled to three layers of clad material that 0.5mm is thick of formation.
Above-mentioned cold rolling alloy can be prepared tempered o material (o-materials) through the process annealing shown in the table 1.Core alloy is by this process annealing perfect recrystallization.The prestrain material generates with depressing than applying strain shown in the table 1 by tension level(l)er (tension lever).As shown in table 1, the prestrain material can thermal treatment or not thermal treatment (annealing at last) after having applied strain.
At first,, done Erichsen test, and measured the height that cracks (profile height (mm)) of sample for assessing the plasticity of each matrix material.Refrigerant flow channel 1 shown in Figure 1 is shaped with the test plasticity by the processing (degree of deformation is 0-15%) that is shaped.The result also is listed in the table 1.
The plate with refrigerant flow channel shape that is shaped is placed on another to be had on the identical shaped plate, and therefore these plates have formed the refrigerant flow channel pipe that refrigerant flow channel is arranged shown in Fig. 1 reference number 2 by heating by soldering.These plates after having covered the fluorine-based flux of one deck, 600 ℃ of down heating 5 minutes in inert gas environment, under such condition by soldering.Can observe the disperse state (penetrating of filler alloys) of filler alloys in the transverse section of refrigerant flow channel pipe.In addition, do the corrosion test of refrigerant flow channel pipe, and behind corrosion test, measured the degree of depth (μ m) of corrosion line.In the corrosion test, constantly carry out following circulation in 1 month, spray 4 hours 5% the sodium chloride aqueous solution (40 ℃, 98%RH) → dry 4 hours (55 ℃, 30%RH) → humidification 4 hours (50 ℃, 98%RH).The result is also in table 1.
Table 1 shows that all matrix materials all show good erosion resistance among the routine 3-15 after corrosion test, the filler alloys that penetrates seldom and the corrosion line very shallow.Haply, in example 1,2, do not observe in the matrix material among the 16-18 filler alloys penetrate and the erosion resistance of matrix material also fine because matrix material has kept 2 hours under 540 ℃ in the process of cooling that homogenization is handled.Owing to carried out last annealing after applying strain, the plasticity of the matrix material of sequence number 3-28 is fine, and finds the crackle of shaping processing.On the other hand, Comparative Examples 1-3 has used homogenization to handle the result who obtains under the condition outside limited range of the present invention, wherein after the corrosion test, penetrating of filler alloys and perforating corrosion pit or very dark corrosion pit have been observed in part with low degree of deformation.In Comparative Examples 4, after the corrosion test, observe penetrating of filler alloys, be accompanied by the appearance in pierceability hole, because should not apply strain in the example.In Comparative Examples 5, the step that matrix material is processed to form the refrigerant flow channel shape causes crackle because compared with the condition defined in the present invention its to give the strained degree of deformation too high.
The industry use-case
Method of the present invention is beneficial to the manufacture method as a kind of Al alloy composite, its processing back brazing product by soldering assembling manufacturing that is used to be shaped.In more detail, this method helps making a kind of material, preferably, such as, a kind of aluminium alloy compound plate is applicable to the flow passage in the vaporizer that forms type in heaps (stacked-type) and the layering of the type oil cooler in heaps in the heat exchanger, or the tube plate of scatterer and similar thing.
Further, Al alloy composite plasticity of the present invention is fine, especially for heat exchanger.In the soldering step, filler alloys to the diffusing capacity of core alloy seldom and the distribution of filler alloys very desirable.Therefore matrix material of the present invention is a kind of preferred Al alloy composite, and the physical strength after its soldering, erosion resistance and plasticity are all fine.
Described our invention according to present embodiment, be noted that this invention is not limited to described details, unless otherwise indicated, can in the spirit and scope that its claim is stated, make up widely.
Table 1
| The homogenization condition | Process annealing | ||||||
| Outlet temperature (℃) | Hold-time (hour) | Cooling conditions has recovery (resetting): non-restoring in 540 ℃ * 2 hours: slowly cooling | Heating rate | Outlet temperature (℃) | Hold-time | Rate of cooling | |
| Example 1 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 2 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 3 | 540 | 18 | Slowly cooling | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour |
| Example 4 | 540 | 18 | Slowly cooling | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour |
| Example 5 | 540 | 18 | Slowly cooling | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour |
| Example 6 | 540 | 18 | Slowly cooling | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour |
| Example 7 | 540 | 18 | Slowly cooling | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour |
| Example 8 | 540 | 18 | Slowly cooling | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour |
| Example 9 | 540 | 18 | Slowly cooling | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 10 | 540 | 18 | Slowly cooling | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 11 | 540 | 18 | Slowly cooling | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 12 | 540 | 18 | Slowly cooling | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 13 | 540 | 18 | Slowly cooling | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 14 | 540 | 18 | Slowly cooling | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 15 | 540 | 18 | Slowly cooling | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 16 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 17 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 18 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 19 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 20 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 21 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 22 | 600 | 16 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Example 23 | 600 | 16 | Restore | 40 ℃/hour | 380 | 2 hours | 40 ℃/hour |
| Example 24 | 600 | 16 | Restore | 40 ℃/hour | 380 | 2 hours | 40 ℃/hour |
| Example 25 | 600 | 16 | Restore | 40 ℃/hour | 380 | 2 hours | 40 ℃/hour |
| Example 26 | 600 | 16 | Restore | 40 ℃/hour | 380 | 2 hours | 40 ℃/hour |
| Example 27 | 600 | 3 | Restore | 40 ℃/hour | 380 | 2 hours | 40 ℃/hour |
| Example 28 | 600 | 3 | Restore | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Comparative Examples 1 | 520 | 14 | Slowly cooling | 120 ℃/hour | 400 | 2 hours | 120 ℃/hour |
| Comparative Examples 2 | 600 | 8 | Slowly cooling | 120 ℃/hour | 400 | 2 hours | 120 ℃/hour |
| Comparative Examples 3 | 600 | 3 | Slowly cooling | 40 ℃/hour | 380 | 2 hours | 40 ℃/hour |
| Comparative Examples 4 | 600 | 16 | Slowly cooling | 80 ℃/minute | 480 | 10 seconds | 80 ℃/minute |
| Comparative Examples 5 | 600 | 16 | Slowly cooling | 40 ℃/hour | 380 | 2 hours | 40 ℃/hour |
Table 1 (continuing)
| Prestrain amount (%) | Last annealing conditions | Penetrating of filler alloys | The corrosion line degree of depth (μ m) after the corrosion test | The profile height of Erichsen test (mm) | Plasticity | |||||
| Heating rate | Final temp (℃) | Hold-time | Rate of cooling | |||||||
| Example 1 | 2.0 | There is not last annealing | ◎ | 64 | 8.8 | ○ | ||||
| Example 2 | 3.0 | There is not last annealing | ◎ | 61 | 8.6 | ○ | ||||
| Example 3 | 2.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ○ | 70 | 9.1 | ◎ | |
| Example 4 | 4.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ○ | 68 | 9.0 | ◎ | |
| Example 5 | 8.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ○ | 71 | 9.1 | ◎ | |
| Example 6 | 2.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ○ | 71 | 9.0 | ◎ | |
| Example 7 | 4.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ○ | 70 | 9.1 | ◎ | |
| Example 8 | 8.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ○ | 70 | 9.1 | ◎ | |
| Example 9 | 2.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ○ | 70 | 9.7 | ◎ | |
| Example 10 | 2.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ○ | 74 | 9.4 | ◎ | |
| Example 11 | 4.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ○ | 65 | 9.6 | ◎ |
| Example 12 | 4.0 | 40 ℃/hour | 350 | 2 hours | 40 ℃/hour | ○ | 69 | 9.4 | ◎ |
| Example 13 | 4.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ○ | 67 | 9.3 | ◎ |
| Example 14 | 8.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ○ | 64 | 9.2 | ◎ |
| Example 15 | 8.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ○ | 65 | 9.0 | ◎ |
| Example 16 | 2.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ◎ | 61 | 9.9 | ◎ |
| Example 17 | 2.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ◎ | 65 | 9.7 | ◎ |
| Example 18 | 4.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ◎ | 52 | 9.7 | ◎ |
| Example 19 | 4.0 | 40 ℃/hour | 300 | 2 hours | 40 ℃/hour | ◎ | 55 | 9.5 | ◎ |
| Example 20 | 4.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ◎ | 59 | 9.5 | ◎ |
| Example 21 | 8.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ◎ | 51 | 9.3 | ◎ |
| Example 22 | 8.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ◎ | 59 | 9.2 | ◎ |
| Example 23 | 2.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ◎ | 53 | 9.8 | ◎ |
| Example 24 | 2.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ◎ | 52 | 9.6 | ◎ |
| Example 25 | 4.0 | 40 ℃/hour | 250 | 4 hours | 40 ℃/hour | ◎ | 54 | 9.7 | ◎ |
| Example 26 | 4.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ◎ | 51 | 9.5 | ◎ |
| Example 27 | 4.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ○ | 77 | 9.5 | ◎ |
| Example 28 | 4.0 | 80 ℃/minute | 350 | 10 seconds | 80 ℃/minute | ○ | 75 | 9.5 | ◎ |
| Comparative Examples 1 | 2.0 | There is not last annealing | × | Perforation | 7.5 | ○ | |||
| Comparative Examples 2 | 2.0 | There is not last annealing | × | Perforation | 7.4 | ○ | |||
| Comparative Examples 3 | 2.0 | There is not last annealing | × | 350 | 8.5 | ○ | |||
| Comparative Examples 4 | 0 | There is not last annealing | × | Perforation | 7.6 | ○ | |||
| Comparative Examples 5 | 11 | There is not last annealing | ◎ | Form crackle in the shaping | |||||
Noting) the penetrating of filler alloys: ◎ do not have and penetrates, and zero penetrates on a small quantity, * penetrate
Plasticity: ◎ does not have crackle, and zero does not have crackle, but extensibility is poor
Claims (7)
1. manufacture method that is used for an Al alloy composite of a heat exchanger may further comprise the steps:
By with an aluminium alloy core alloy 530 ℃ or higher maintenance 15 hours or longlyer come homogenizing aluminium alloy core alloy;
A side or both sides at the aluminium alloy core alloy cover an aluminium silicon series alloy;
The coating alloy that hot rolling generates;
The coating alloy of cold rolling hot rolling;
The coating alloy of cold rolling mistake is carried out the process annealing processing so that the abundant recrystallize of aluminium alloy core alloy;
Apply the strain of 1-10% for the alloy that generates, wherein the mass percent of aluminium alloy core alloy (being reduced to % hereinafter) comprises the silicon of 0.01-1.0%, the iron of 0.1-2.0%, the copper of 0.1-2.0%, the manganese of 0.5-2.0%, be less than 0.2% and more than or equal 0% titanium, remaining sum is aluminium and unavoidable impurities.
2. the method for claim 1, wherein said process annealing comprise that the coating alloy with cold rolling mistake kept 1 hour or more at 320-450 ℃.
3. the method for claim 1, wherein said process annealing comprises: with 30 ℃/minute or faster rate of heating heat the coating alloy of cold rolling mistake; Under 300-550 ℃, coating alloy is kept 1-180 second; The alloy that generates with 30 ℃/minute or speed of cooling cooling faster then.
4. as any described method in the claim 1 to 3, wherein after applying the strained step of 1-10%, also comprised heat treated step.
5. method as claimed in claim 4, wherein after the strain that applies 1-10%, described thermal treatment is included in 200-380 ℃ and kept 1 hour or longer.
6. method as claimed in claim 4, wherein after applying the strained of 1-10%, described thermal treatment comprises that step has: with 30 ℃/minute or rate of heating heating faster; Keep 1-180 second down at 250-420 ℃; Then with 30 ℃/minute or speed of cooling cooling faster.
7. one kind with the Al alloy composite that is used for heat exchanger that produces as the described method of claim 1-6.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP64398/2002 | 2002-03-08 | ||
| JP2002064398A JP4053793B2 (en) | 2002-03-08 | 2002-03-08 | Manufacturing method of aluminum alloy composite for heat exchanger and aluminum alloy composite |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2006101517275A Division CN100425726C (en) | 2002-03-08 | 2003-03-06 | Method for producing aluminum alloy composite material for heat exchanger and aluminum alloy composite material |
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| Publication Number | Publication Date |
|---|---|
| CN1639372A CN1639372A (en) | 2005-07-13 |
| CN1321217C true CN1321217C (en) | 2007-06-13 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB038050331A Expired - Fee Related CN1321217C (en) | 2002-03-08 | 2003-03-06 | Method for producing aluminum alloy composite material for heat exchanger and aluminum alloy composite material |
| CNB2006101517275A Expired - Fee Related CN100425726C (en) | 2002-03-08 | 2003-03-06 | Method for producing aluminum alloy composite material for heat exchanger and aluminum alloy composite material |
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| CNB2006101517275A Expired - Fee Related CN100425726C (en) | 2002-03-08 | 2003-03-06 | Method for producing aluminum alloy composite material for heat exchanger and aluminum alloy composite material |
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| Country | Link |
|---|---|
| US (1) | US20050067066A1 (en) |
| EP (1) | EP1484425B1 (en) |
| JP (1) | JP4053793B2 (en) |
| KR (1) | KR100955159B1 (en) |
| CN (2) | CN1321217C (en) |
| DE (1) | DE60329170D1 (en) |
| WO (1) | WO2003076677A1 (en) |
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- 2003-03-06 WO PCT/JP2003/002652 patent/WO2003076677A1/en active Application Filing
- 2003-03-06 CN CNB2006101517275A patent/CN100425726C/en not_active Expired - Fee Related
- 2003-03-06 DE DE60329170T patent/DE60329170D1/en not_active Expired - Lifetime
- 2003-03-06 KR KR1020047014016A patent/KR100955159B1/en active IP Right Grant
- 2003-03-06 EP EP03710263A patent/EP1484425B1/en not_active Expired - Lifetime
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Also Published As
| Publication number | Publication date |
|---|---|
| EP1484425A1 (en) | 2004-12-08 |
| CN1639372A (en) | 2005-07-13 |
| CN100425726C (en) | 2008-10-15 |
| WO2003076677A1 (en) | 2003-09-18 |
| CN1936060A (en) | 2007-03-28 |
| JP4053793B2 (en) | 2008-02-27 |
| EP1484425B1 (en) | 2009-09-09 |
| DE60329170D1 (en) | 2009-10-22 |
| US20050067066A1 (en) | 2005-03-31 |
| KR20040101275A (en) | 2004-12-02 |
| JP2003268512A (en) | 2003-09-25 |
| EP1484425A4 (en) | 2005-06-29 |
| KR100955159B1 (en) | 2010-04-28 |
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